EP2724995A1 - Transparente, eingefärbte Kochflächen - Google Patents

Transparente, eingefärbte Kochflächen Download PDF

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Publication number
EP2724995A1
EP2724995A1 EP13186925.7A EP13186925A EP2724995A1 EP 2724995 A1 EP2724995 A1 EP 2724995A1 EP 13186925 A EP13186925 A EP 13186925A EP 2724995 A1 EP2724995 A1 EP 2724995A1
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EP
European Patent Office
Prior art keywords
glass
cooking surface
temperature
display
red
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EP13186925.7A
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German (de)
English (en)
French (fr)
Inventor
Friedrich Dr. Siebers
Thomas Dr. Zenker
Helga Goetz
Martin Taplan
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Schott AG
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Schott AG
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Application filed by Schott AG filed Critical Schott AG
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    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/0054—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing PbO, SnO2, B2O3
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/0018—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and monovalent metal oxide as main constituents
    • C03C10/0027—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and monovalent metal oxide as main constituents containing SiO2, Al2O3, Li2O as main constituents
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/0036—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and a divalent metal oxide as main constituents
    • C03C10/0045—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and a divalent metal oxide as main constituents containing SiO2, Al2O3 and MgO as main constituents
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/009—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition having a superconducting crystal phase
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F24—HEATING; RANGES; VENTILATING
    • F24C—DOMESTIC STOVES OR RANGES ; DETAILS OF DOMESTIC STOVES OR RANGES, OF GENERAL APPLICATION
    • F24C15/00—Details
    • F24C15/10—Tops, e.g. hot plates; Rings

Definitions

  • the invention relates to a transparent, colored cooking surface consisting of a glass ceramic with high-silica solid solution crystals as the predominant crystal phase and to a process for their preparation.
  • Such glass ceramic plates are usually in the form of flat plates or are deformed three-dimensionally.
  • Glass ceramics with high quartz mixed crystals as the predominant crystal phase are prepared from crystallizable lithium aluminum silicate glasses.
  • the crystallizable starting glass is first melted from a mixture of shards and pulverulent mixed raw materials at temperatures usually between 1500 and 1650 ° C.
  • Arsenic and / or antimony oxide is typically used as the refining agent in the melt.
  • These refining agents are compatible with the required glass-ceramic properties and lead to good bubble qualities of the melt. Even if these substances are firmly bound in the glass framework, they are disadvantageous in terms of safety and environmental protection. For example, special precautionary measures must be taken in the extraction, treatment and evaporation of the melt.
  • the glass After melting and refining, the glass usually undergoes hot forming by rolling or, more recently, floating to make sheets.
  • a low melting temperature and a low processing temperature V A are desired, on the other hand, the glass must not show any devitrification during shaping. This means that no disruptive crystals must form which impair the strength in the starting glasses and the glass ceramics produced therefrom. Since the shaping takes place near the processing temperature V A (viscosity 10 4 dPas) of the glass, it must be ensured that the upper devitrification temperature of the melt is in the vicinity and favorably below the processing temperature in order to avoid the formation of troublesome crystals.
  • the starting glass is transferred by controlled crystallization in the glass-ceramic article.
  • This ceramization takes place in a two-stage temperature process in which nuclei, usually from ZrO 2 / TiO 2 mixed crystals, are initially produced by nucleation at a temperature of between 680 and 800 ° C. SnO 2 may also be involved in nucleation.
  • the high-quartz mixed crystals grow on these nuclei.
  • High crystal growth rates, as desired for economical, rapid ceramification are achieved at temperatures of 850 to 950 ° C. At this maximum production temperature, the microstructure of the glass-ceramic is homogenized and the optical, physical and chemical properties of the glass-ceramic are adjusted.
  • the high quartz mixed crystals can subsequently be converted into keatite mixed crystals.
  • the conversion into keatite mixed crystals takes place at a temperature increase in a range of about 950 to 1200 ° C.
  • the thermal expansion coefficient of the glass-ceramic increases and the transparency is reduced by the light scattering associated with the enlargement of the crystals.
  • glass ceramics with keatite mixed crystals as the main phase are therefore translucent or opaque, and the associated light scattering adversely affects the readability.
  • a key property of these glass ceramics with high quartz mixed crystals as the main crystal phase is the manufacturability of materials that have a very low coefficient of thermal expansion in the range of room temperature to 700 ° C and above of ⁇ 0.5 x 10 -6 / K. Due to the low thermal expansion, these glass ceramics have excellent temperature difference resistance and thermal shock resistance.
  • the glass ceramic cooking surfaces are limited in their light transmission.
  • the cooling of the heating elements after annealing is no longer visible, although the heat capacity of the materials used and present still considerable heat is present, which is sufficient to cause serious injury.
  • a certain light transmission is required because the usual red LEDs are installed below the hotplate.
  • glass ceramic cooktops are usually set to levels of light transmission of 0.5 to 2.5%. This is achieved by adding coloring elements. Glass ceramic cooktops then appear regardless of the color element used in black because of the low light transmission, in review, depending on the color elements used usually red, reddish purple or brown orange.
  • Colored displays consist of light-emitting electronic components, usually light-emitting diodes, which are installed below the cooking surface. They are for ease of use and the safe operation desired. For example, the current heat output or residual heat of the various cooking zones are visually displayed. The display of residual heat is important for safe handling if the radiators do not radiate or if, as with inductively heated cooking surfaces is generally not detectable that the cooking surface is hot.
  • the usual red LEDs radiate at wavelengths around 630 nm. In order to improve the ease of use and the technical features, but also to open the home appliance manufacturers on the design a way to differentiate, in addition to the usual red and other colored displays are desired.
  • Safety-relevant information is coded and known only via the same-colored display elements or symbols in seven-segment displays. In safety-critical situations, the user is forced to think about what the ad wants to show him. This is in addition to the fact that due to the high degree of technology in kitchens and the variety of existing appliances in kitchens, such as cookers, ovens, microwaves, grills, cooker hoods, refrigerators and freezers and bread slicing machines, etc., a flood of information acts on the user Information varies from device to device. For example, a red flashing light in one device may pose a hazard while indicating operation on the other device.
  • a user can not recognize the operating and error state via the colors, ie to what extent the device is ready for operation and whether there is an indication of a possible error state.
  • a high transmission in the infrared is advantageous because the radiation hits directly on the bottom of the pot, is absorbed there and thus faster boiling is achieved. If the transmission is too high, the environment of the cooking surface may be in the event of operating errors, eg. B. at free-radiating cooking zone by a suspended pot to overheat.
  • Ceran Color® An earlier type of glass ceramic cooking surfaces, known under the name Ceran Color® , manufactured by SCHOTT AG, had good color display capability. Ceran Color® is colored by additions of NiO, CoO, Fe 2 O 3 and MnO and purified by Sb 2 O 3 . By this combination of color oxides, a light transmission of typically 1.2% is set for cooking surfaces with usual thickness of 4 mm. The transmission in the range of 380 nm to 500 nm, depending on the wavelength 0.1 - 2.8%. At a wavelength of 630 nm usual for red LEDs, the transmission is about 6%. A disadvantage of this earlier type of glass ceramic cooktops is that the color oxides used also absorb very strongly in the infrared. The IR transmission at 1600 nm is less than 20%.
  • vanadium is incorporated into the seed crystal as V 4+ or V 3+ in a reduced oxidation state and stains intensely there by means of electron charge transfer reactions.
  • TiO 2 can also enhance the coloration by vanadium oxide.
  • the redox state which is set in the glass in the melt also has an influence.
  • a low partial pressure of oxygen pO 2 (reducing set melt), for example by high melting temperatures enhances the color effect of vanadium oxide.
  • V 2 O 5 The described relationships in coloring by V 2 O 5 will be used by one skilled in the art in order to set the desired transmission profile by means of a specific glass composition, specific redox settings of the pO 2 in the melt and the ceramization conditions. So far, however, it has not been possible to meet all requirements such as specification-compliant light transmission, high IR transmission, as well as display capability for standard red LEDs, together with the desired improved display capability for different colored lights.
  • the shape of the absorption band of the vanadium oxide and thus the transmission in the visible light range in the entire wavelength range greater than 450 nm up to the upper limit of 750 nm could not be adapted to higher transmissions.
  • V 2 O 5 -stained glass ceramic cooking surface types examples include the Sb 2 O 3 ceramic -geläuterte Hightrans ® and the Sn02-purified ceramic Suprema ®, which are manufactured by SCHOTT AG.
  • the transmission curves of these two glass-ceramics are published in the book " Low Thermal Expansion Glass Ceramics ", Second Edition, Editor Hans Bach, Dieter Krause, Springer-Verlag Berlin Heidelberg 2005, on page 63 (ISBN 3-540-24111-6 ).
  • the transmission value of 0.1% is below the mentioned glass-ceramic cooktops and other glass-ceramic cooktops on the market in the wavelengths of about 450-550 nm, which are important for the visibility of colored, in particular blue and green displays.
  • Other essential requirements for the transmission are fulfilled by these glass-ceramic cooking surfaces: high infrared transmission for high heating speeds, specification-compliant transmission for standard red light-emitting diodes at approx. 630 nm and a light transmission of 1.5%.
  • the cooking surfaces according to the invention are intended to meet all other requirements placed on cooking surfaces, such as chemical resistance, temperature resistance and high temperature / time resistance to changes in their properties (such as thermal expansion, transmission, stress build-up).
  • the colored cooking surfaces have transmission values of greater than 0.1% in the visible light range over the entire wavelength range of greater than 450 nm, a light transmission in the visible range of 0.8-5% (preferably 0.8-2.5%) and a transmission in the infrared at 1600 nm of 45-85%.
  • the light transmission according to the invention ensures that the disturbing view of the technical components under the glass ceramic cooking surface is prevented and the aesthetic black appearance is ensured in the top view.
  • Radiating radiators are visible during operation and common red LED displays are clearly visible. Due to the transmission of greater than 0.1% in the range of visible light throughout Wavelength range greater than 450 nm, even differently colored displays are clearly visible. Given the luminosity of commercially available blue, green, yellow or orange LEDs, this transmission value is sufficient and represents a significant improvement over the prior art. In particular, the display with blue and green colors is significantly improved. Displays with white light are less falsified by the transmission profile in the entire wavelength range greater than 450 nm.
  • the display elements radiate their light from the back of the cooking surface ago and this is then perceived accordingly on the front of the viewer.
  • the transmission behavior of the cooking surface thus allows a clear representation of different heat conditions and / or error conditions.
  • the display which gives a red, orange or blue color impression depending on the heat.
  • the red color stands for heat, the orange color for heat and a blue color design for cold.
  • the display has a red-illuminating, possibly orange-illuminating and possibly a blue-emitting field, which are formed in particular from LEDs.
  • a luminous field in which a color change within a single field or along different color fields or segments continuously running precipitates.
  • such color patches which have either different individual color patches or a single color pel, can indicate defect states.
  • red means a safety-critical fault state or operating state
  • yellow a fault state which is not safety-critical, and green unrestricted operational readiness.
  • the low transmission values of significantly less than 0.01% of the known glass-ceramic cooking surfaces are also ensured with the cooking surface according to the invention.
  • the blocking of the UV light is advantageous for protecting organic components, e.g. Glue in the technical installations under the cooking surface, as well as protection during cooking, if blue light emitting diodes with ultraviolet radiation portion are used for display.
  • the transmission and light transmission values according to the invention are decisive for the function of the cooking surface, they are independent of the thickness of the cooking surface, which is usually between 2.5 and 6 mm. Smaller thicknesses are disadvantageous in terms of strength and larger thicknesses are uneconomical because they require more material and reduce the ceramization speed. Usually the thickness of the cooking surface is about 4 mm.
  • the specified transmission values for commercial cooking surfaces and in the embodiments therefore, unless otherwise stated, refer to this thickness.
  • the underside is usually studded to protect it from compromising strength in manufacture.
  • the underside of the cooking surface in the area of the colored displays is smoothed with transparent organic polymer in order to avoid optical distortion from the nubs. For cooking surfaces with a smooth underside without nubs, colored displays are undistorted and lighter.
  • the cooking surfaces according to the invention have low coefficients of thermal expansion of less than 1 ⁇ 10 -6 / K, preferably of (0 ⁇ 0.3) ⁇ 10 -6 / K.
  • the transparent, colored cooking surfaces according to the invention are thus characterized by a composition without the use of arsenic and / or antimony oxide as refining agent and are thus technically free of these under adverse environmental and safety aspects disadvantageous components.
  • these components are usually present at levels of less than 500 ppm.
  • the inventive method for producing a transparent, colored cooking surface with improved color display capability is characterized in that it forms a glass ceramic with high-quartz mixed crystal as the predominant crystal phase and that is dispensed with unavoidable traces on the chemical refining arsenic and / or antimony oxide and the cooking surface to transmission values of greater than 0.1% in the visible light range over the entire wavelength range greater than 450 nm, visible light transmission of 0.8 to 2.5% and infrared transmission at 1600 nm from 45 to 85 % is set.
  • further refining additives such as CeO 2 , sulfate compounds, halide compounds, can be used to improve the quality of the bubbles.
  • Their contents are usually in amounts of up to 1% by weight. limited. In the production of cooking surfaces, those with bubble numbers of less than 10, preferably less than 5 bubbles / kg of glass (based on bubble sizes greater than 0.1 mm) are desired as good bubble qualities.
  • the color display capability is further improved and the different demands on the transmission process are further optimized.
  • a further improved coverage of the technical installations below the cooking surface glass ceramic and a particularly aesthetic black appearance in incident light is achieved when the light transmission is less than 1.7%.
  • Transmission values of the cooking surface at 630 nm of 3 to 9% correspond to the tolerance values of commercially available cooking surfaces. It is advantageous to set these values, so that the appearance of the conventional red LED displays is unchanged even in the cooking surface according to the invention.
  • the cooking surface according to the invention preferably has a composition of the glass ceramic which in wt .-% based on oxide essentially consists of: Li 2 O 3.0 - 4.2 ⁇ Na 2 O + K 2 O 0.2-1.5 MgO 0 - 1.5 ⁇ CaO + SrO + BaO 0 - 4 ZnO 0 - 2 B 2 O 3 0 - 2 Al 2 O 3 19-23 SiO 2 60 - 69 TiO 2 2,5 - 4 ZrO 2 0,5 - 2 P 2 O 5 0 - 3 SnO 2 0.1 - ⁇ 0.6 ⁇ TiO 2 + ZrO 2 + SnO 2 3.8 - 6 V 2 O 5 0.01-0.06 Fe 2 O 3 0.03 - 0.2, under the condition: 1 ⁇ Fe 2 ⁇ O 3 / V 2 ⁇ O 5 ⁇ 8th.
  • the term “consisting essentially of” means that the listed components should be at least 96%, typically 98% of the total composition.
  • a variety of elements such as e.g. F, Cl, the alkalies Rb, Cs or elements such as Hf are common impurities in the case of the bulk raw materials used.
  • Other compounds e.g. those of the elements Ge, rare earths, Bi, W, Nb, Ta, Y can be added in small amounts.
  • the absorption band of Nd in the near infrared at 806 nm is in a range of high transmission values of the glass-ceramic and is thus prominent in the transmission spectrum.
  • the cooking surface material can be safely assigned to the manufacturer and with optical cullet detection method, a good recycling is possible.
  • the water content of the starting glasses for producing the cooking surfaces according to the invention is usually between 0.015 and 0.06 mol / l, depending on the choice of the batch raw materials and the process conditions in the melt. This corresponds to ⁇ -OH values of 0.16 to 0.64 mm -1 for the starting glasses.
  • the oxides Li 2 O, Al 2 O 3 and SiO 2 in the preferred limits given are necessary components of the high quartz mixed crystals.
  • a minimum content of Li 2 O of 3 wt .-% is required, but lead Li 2 O contents of over 4.2 wt .-% in a manufacturing process often to unwanted devitrification.
  • a content of 3.2 to 4.0 wt .-% leads to particularly good results.
  • the Al 2 O 3 content is limited to preferably not more than 23% by weight, in particular 22% by weight.
  • the SiO 2 content to a maximum of 69 wt .-%, respectively, since this component greatly increases the viscosity of the glass.
  • this component is further limited to values of at most 68 and further at most 67 wt .-%.
  • the minimum content of SiO 2 should be 60% by weight, in particular 62% by weight, because this is advantageous for the required cooking surface properties, such as eg chemical resistance and temperature resistance.
  • MgO, ZnO and P 2 O 5 can be incorporated into the high quartz mixed crystals.
  • the ZnO content is limited to values of not more than 2.0% by weight, preferably not more than 1.8% by weight, during the ceramization because of the problem of the formation of undesired crystal phases such as zinc spinel (Gahnit).
  • the MgO content is limited to a maximum of 1.5 wt .-%, preferably up to 1.2 wt .-%, because he otherwise increases the expansion coefficient of the glass ceramic inadmissible.
  • An MgO minimum content of 0.1 wt .-% is usually required so that the thermal expansion of the glass ceramic does not fall to negative values.
  • alkalis Na 2 O, K 2 O and the alkaline earths CaO, SrO, BaO and B 2 O 3 improves the meltability and the devitrification stability in the shaping of the glass.
  • the contents must be limited because these components are not incorporated into the crystal phases, but remain essentially in the residual glass phase of the glass ceramic.
  • the sum of the alkalis Na 2 O + K 2 O should be at least 0.2, preferably at least 0.4 wt .-% and at most 1.5 wt .-%, preferably at most 1.2 wt .-%.
  • the sum of the alkaline earths CaO + SrO + BaO should be at most 4% by weight, preferably at least 0.2% by weight.
  • the mentioned alkalis and alkaline earths accumulate, except in the residual glass phase between the crystals, also on the surface of the glass ceramic.
  • ceramizing forms an approximately 200 to 1000 nm thick glassy surface layer that almost is free of crystals and which is enriched in these elements and depleted of lithium. This glassy surface layer has a favorable effect on the chemical resistance of the glass ceramic.
  • the addition of P 2 O 5 may be up to 3% by weight and is preferably limited to 1.5%.
  • the addition of P 2 O 5 is favorable for the devitrification resistance. Higher contents have an unfavorable effect on the acid resistance.
  • TiO 2 , ZrO 2 and SnO 2 are required as nucleating agents. During the ceramization they form germs in high density during nucleation, which serve as a substrate for the growth of the high quartz mixed crystals during crystallization. Higher contents than the sum of 6% by weight deteriorate the devitrification stability. This is especially true for the SnO 2 component, which is limited to values less than 0.6% by weight. Higher contents lead to the crystallization of Sn-containing crystal phases on the contact materials (eg Pt / Rh) during shaping and must be avoided at all costs.
  • the contact materials eg Pt / Rh
  • the ZrO 2 content is limited to 2% by weight, preferably 1.8% by weight and more preferably to a maximum of 1.6% by weight, since higher contents worsen the melting behavior of the mixture during glass production and the devitrification stability
  • the shaping can be affected by the formation of ZrO 2 - containing crystals.
  • the minimum content of ZrO 2 should be 0.5% by weight and preferably 0.8% by weight in order to promote a high ceramization rate.
  • the TiO 2 content is between 2.5 and 4.0 wt .-%, preferably at least 2.8 wt .-%.
  • the minimum amount should not be undershot, so that rapid nucleation is ensured for achieving high Kerammaschines Anlagenen.
  • the content should not exceed 4% by weight because otherwise the devitrification stability is deteriorated.
  • Fe 2 O 3 contents from 600 ppm, preferably from 700 ppm, in combination with tightly specified contents of TiO 2 , V 2 O 5 and SnO 2 can influence the transmission profile. Since Fe 2 O 3 , especially the proportion of divalent Fe 2+ has a negative effect on the IR transmission, the Fe 2 O 3 content at most 0.2 and preferably at most 0.18 wt .-% amount. Particularly preferred is a Fe 2 O 3 content of 0.08 to 0.15 wt .-%.
  • the combination of the color oxides Fe 2 O 3 with V 2 O 5 and its redox partner SnO 2 makes it possible to manage with smaller amounts of the costly and classified as hazardous dye V 2 O 5 .
  • the requirements for transmission at low wavelengths from 450 nm and the other requirements such as specification-compliant light transmission, infrared transmission, and the transmission at 630 nm are met.
  • the transmission curve becomes flatter in the range of visible light compared to the known vanadium oxide-colored glass ceramics.
  • the Fe 2 O 3 content must be at least as high as the V 2 O 5 content and thus satisfy the condition 1 ⁇ Fe 2 ⁇ O 3 / V 2 ⁇ O 5 ⁇ 8th.
  • the color oxide Fe 2 O 3 is quantitatively the main colorant and preferably the content is twice as high as that of the V 2 O 5 .This also makes it possible to use less expensive batch raw materials.
  • V 2 O 5 content Other components that contribute to reducing the required V 2 O 5 content are SnO 2 and TiO 2 .
  • SnO 2 and TiO 2 are SnO 2 and TiO 2 .
  • V 2 O 5 , SnO 2 , TiO 2 and Fe 2 O 3 are set within certain narrow limits.
  • the TiO 2 content must exceed a certain minimum amount.
  • Fe 2 O 3 -, TiO 2 -, V 2 O 5 - and SnO 2 contents according to the invention it is possible to meet all requirements for the transmission profile, such as specification-compliant light transmission, high infrared transmission, and display capability for standard red LEDs together with achieve the desired improved display capability for differently colored lights.
  • Fe 2 O 3 Another important result of the addition of Fe 2 O 3 was found to significantly aid refining. In combination with the SnO 2 as main remedy The Fe 2 O 3 also releases oxygen and is thereby reduced to Fe 2+ .
  • the relevant for the refining effect sales increases with the temperature of the melt. A temperature treatment of the melt greater than 1700 ° C and further greater than 1750 ° C thus provides further improved results in terms of bubble quality.
  • the content should be at least 20% of the SnO 2 content.
  • the proportion of crystal phase-forming components such as Li 2 O, SiO 2 and the proportion of the components which form the residual glass phase of the glass ceramic, such as the alkalis Na 2 O and K 2 O and the alkaline earths CaO, SrO, BaO increase.
  • the proportion of high quartz mixed crystal phase is advantageously less than 70 wt .-% and is 60 to 70 wt .-%.
  • the cooking surface according to the invention preferably has a composition of the glass ceramic which, in terms of weight percent based on oxide, essentially consists of: Ll 2 O 3.2 - 4.2 Na 2 O 0.1 - 1 K 2 O 0.1 - 1 ⁇ Na 2 O + K 2 O 0.2-1.5 MgO 0 - 1.5 ⁇ CaO + SrO + BaO 0.1 - 4 ZnO 0 - 2 B 2 O 3 0 - 1 Al 2 O 3 19-23 SiO 2 60 - 68 TiO 2 2.8 - 4 ZrO 2 0.8-1.8 P 2 O 5 0 - 1.5 SnO 2 0.1 - ⁇ 0.6 ⁇ TiO 2 + ZrO 2 + SnO 2 4,4 - 6 V 2 O 5 0.01-0.05 Fe 2 O 3 0.07 - 0.18, under the condition: 2 ⁇ Fe 2 ⁇ O 3 / V 2 ⁇ O 5 ⁇ 6th
  • a fast ceramisability is understood to mean a thermal treatment for the crystallization of the glass ceramic with a duration of less than 2 hours, preferably less than 80 minutes.
  • the thermally relaxed crystallizable starting glass is heated to the temperature range of about 680 ° C. within 3 to 30 minutes.
  • the required high heating rates can be realized on an industrial scale in roller kilns.
  • This temperature range of about 680 ° C corresponds approximately to the transformation temperature of the glass.
  • Above this temperature to about 800 ° C is the range with high nucleation rates.
  • the temperature range of nucleation is traversed over a period of 10 to 30 minutes.
  • the temperature of the crystallization nuclei-containing glass is increased within 5 to 30 minutes to a temperature of 850 to 950 ° C, which is characterized by high crystal growth rates of the high-quartz solid solution phase. This maximum temperature is maintained for up to 20 minutes.
  • the structure of the glass-ceramic is homogenized and the optical, physical and chemical properties are adjusted.
  • the glass ceramic obtained is cooled to 800 ° C with cooling rates of about 10 ° C / min and then rapidly to room temperature.
  • BaO increases the density of the glass ceramic and thus the weight of the cooking surface.
  • the contents of CaO should be 0.2 to 1% by weight and SrO 0.1 to 1% by weight.
  • the crystallizable starting glass should be readily meltable and have a high devitrification resistance.
  • the processing temperature should be less than 1320 ° C and preferably less than 1310 ° C.
  • the upper devitrification limit should be at least 30 ° C., preferably at least 50 ° C. below the processing temperature.
  • critical crystal phases are mullite (aluminum silicate), Baddeleyt (ZrO 2 ) and Li 2 O-Al 2 O 3 -SiO 2 mixed crystals and SnO 2 -containing crystal phases.
  • the devitrification resistance accordingly, higher contents of Li 2 O, Al 2 O 3 , SiO 2 , ZrO 2 and SnO 2 are disadvantageous.
  • a cooking surface according to the invention preferably has the following composition in% by weight based on oxide: Li 2 O 3.2 - 4.0 Na 2 O 0.2 - 1 K 2 O 0.1 - 1 ⁇ Na 2 O + K 2 O 0.4 - 1.2 MgO 0.1 - 1.2 CaO 0.2 - 1 SrO 0 - 1 BaO 0 - 3 ⁇ CaO + SrO + BaO 0.2 - 4 ZnO 0 - 1.8 B 2 O 3 0 - 1 Al 2 O 3 19-22 SiO 2 62 - 67 TiO 2 2.8 - 4 ZrO 2 0.5 - 1.6 P 2 O 5 0 - 1.5 SnO 2 0.1 - 0.5 ⁇ TiO 2 + ZrO 2 + SnO 2 4,2 - 6 V 2 O 5 0.01-0.05 Fe 2 O 3 0.08 - 0.15, under the condition: 2 ⁇ Fe 2 ⁇ O 3 / V 2 ⁇ O 5 ⁇ 6th
  • the mentioned different requirements for the transmission can then be better coordinated with each other.
  • the equilibrium oxygen partial pressure pO 2 of 1 bar should be achieved at a temperature of> 1580 ° C., preferably of> 1640 ° C. The higher this temperature, the more reducing the glass obtained is adjusted and the proportions of low valences in the polyvalent components such. As Sn 2+ , Fe 2+ , Ti 3+ are increased. This enhances the color effect of the vanadium oxide.
  • This equilibrium oxygen partial pressure pO 2 can be adjusted in the melt by addition of reducing agents in powdery and / or liquid form to the starting mixture.
  • reducing agents metals, carbon and / or oxidizable carbon or metal compounds such as Al or Si powder, sugar, charcoal, SiC, TiC, MgS, ZnS are suitable.
  • Gaseous reducing agents, such as forming gas are suitable. The abovementioned reducing agents are suitable for lowering the pO 2 of the melt and setting the desired value for the equilibrium oxygen partial pressure.
  • a preferred way to set the equilibrium oxygen partial pressure pO 2 is the temperature treatment of the molten glass at temperatures of greater than 1700 ° C, preferably greater than 1750 ° C.
  • This temperature treatment can be advantageously carried out as a high-temperature refining, which allows to achieve the desired low bubble numbers of ⁇ 10, preferably ⁇ 5 bubbles / kg on an industrial scale.
  • the lautering effect is so pronounced because the SnO 2 is a refining agent that releases the required for refining oxygen at high temperatures above 1700 ° C amplified.
  • the temperature at which the equilibrium oxygen partial pressure pO 2 is 1 bar has the maximum temperature in the treatment. Since this equilibrium is not fully achieved in the large-scale glass melt and the throughputs used for reasons of time, always a certain amount of oxygen lautering bubbles remains in the melt and is absorbed on cooling. Furthermore, to a lesser extent, oxygen from the environment is resumed upon cooling the melt from the maximum temperature to the forming temperature VA. As a result, the measured temperature of the equilibrium oxygen partial pressure pO 2 of 1 bar does not correspond to the maximum temperature at the melt, but is lower. Unless you add reducing additives.
  • one or more differently colored displays such as blue, green, yellow, orange or white are arranged instead of or in addition to the usual red displays.
  • the colored displays consist of light-emitting electronic components, mostly of light-emitting diodes.
  • the bottom of the cooking surface may have the usual knobs or smooth.
  • the user is supported by the use of symbols or text in the evaluation of the error state.
  • heat flame symbol
  • a temperature indicator panel that is lit red may also have a large flame in the display panel. The corresponding orange panel has a small flame and the blue box has no icon or icon symbolizing the cold.
  • the indicators may flash and, in particular, blink faster or slower or in different rhythms depending on the error and / or temperature intensity.
  • the cooking surface can be heated by radiant heaters, halogen radiators, induction heating or with gas. There are all forms of ads, punctual as well as area possible.
  • the cooking surface can not only be formed as a flat plate, but also three-dimensionally deformed such. beveled, angled or curved plates can be used.
  • the plates may be rectangular or in other shapes, and in addition to planar regions, three-dimensionally deformed regions such as e.g. Woks included.
  • Table 1 lists compositions and properties of crystallizable starting glasses.
  • the glasses 1 to 12 are glasses according to the invention and the glass 13 is a comparative glass outside the present invention whose composition corresponds to the commercial cooktop glass ceramic Ceran Suprema® from SCHOTT AG.
  • the compositions do not exactly add up to 100% by weight.
  • Typical impurities although not intentionally introduced into the composition, are F, Cl, B, P, Rb, Cs, Hf, which are usually less than 0.05% by weight. They are often introduced via the raw materials for the chemically related components, e.g. Rb and Cs via the Na or K raw materials, or Sr over the Ba raw material and vice versa.
  • the water content of the glasses is 0.03-0.05 mol / l, corresponding to ⁇ OH values of 0.32 to 0.53 mm -1 .
  • the glasses are melted in Pt / Rh 10 crucibles. Subsequently, the crucibles are kept at different temperatures in the range of the processing temperature V A for 5 hours. The uppermost temperature at which the first crystals at the contact surface of the molten glass occur to the crucible wall determines the devitrification temperature.
  • the maximum temperature of the melt and the associated time, and the measured temperature are listed at the pO 2 reaches the value 1 bar.
  • the pO 2 is a function of the temperature and is reversibly dependent on it, as long as no oxygen is exchanged with the environment.
  • the starting glasses of Table 1 were melted from conventional raw materials in the glass industry at temperatures of about 1620 ° C, 4 hours. After melting the mixture into crucibles made of sintered silica glass, the melts were recast in Pt / Rh crucible with inner crucible made of silica glass and homogenized by stirring at temperatures of 1550 ° C, 30 minutes. After this homogenization, various temperature treatments were performed for refining. The maximum melting or refining temperatures and times are shown in Table 1.
  • the glasses 1, 2, 3 and 7, 8 and 9, 10 are the same compositions, which were melted differently.
  • Glass 1 was subjected to a high temperature explanation.
  • Glass 3 was made more reducible by addition of 1% by weight of sugar to the mixture over the glass No. 2 refined at the same temperatures. Consequently, the temperatures for the equilibrium oxygen partial pressure also differ. Due to the different, reducing conditions of the crystallizable starting glasses associated therewith, the transmission values of the glass ceramics obtained differ with the same ceramizing conditions. At low maximum temperatures of the melt, higher proportions of V 2 O 5 or higher ceramization temperatures are needed to match the transmission values.
  • the glasses 1, 4 and the comparative glass 12, as well as shards of the commercially produced glass ceramic Ceran Color ® were after refining and standing at 1600 ° C, 50 h in a 14 l capacity Pt / Rh10 crucible with a laboratory roll mill molded cooking surfaces typical plates.
  • the laboratory roller consists of shortened original production rollers.
  • the lower roller is structured to produce a common dimpled cooking surface base.
  • the test specimens for the measurements and plates of dimension 18 cm x 18 cm x 4 mm for the investigations of flatness are at a faster after cooling to reduce stresses Ceramization prepared.
  • the plates were ceramized in a laboratory furnace with homogeneous, controllable top and bottom heat on a flat ceramic base plate. It was heated at 10 ° C / min to 750 ° C, holding time 15 min. The mixture was then further heated at 4 ° C./min to 900 ° C., holding time 15 minutes and cooled rapidly to room temperature. Throughout the program, the upper temperature in the oven was 6 ° C higher than the bottom.
  • the glass ceramic plates were deliberately deformed like a dome.
  • the deviation from the flatness for the comparative glass No. 13 was 2.1 ⁇ 0.2 mm (6 experiments), for Ceran Color® 0.6 ⁇ 0.1 mm (4 tests) and for glass No. 1 and No. 4 for both 0.5 ⁇ 0.1 mm (3 experiments).
  • Ceramic Color ® is that it can be ceramize in less than 80 minutes with the required flatness, this is shown by the relative experimental comparison for the inventive glasses.
  • Table 2 shows the ceramification conditions and properties of the obtained glass-ceramics and comparative ceramics 2, 4, 17, outside the invention.
  • the ceramization of the starting glasses was carried out with the following temperature / time programs, the values for T max and t max are given in Table 2:
  • Example 3 This can be corrected by adjusting the ceramification conditions (Examples 3 and 5).
  • the starting glasses Nos. 1, 2 and 3 of Examples 1 to 5 have the same composition and differ only in the set in the melt redox state.
  • the values for the average crystallite size and the proportion of the high quartz mixed crystal phase were determined by X-ray diffraction.
  • the examples Because of their content of high-quartz mixed crystal as the predominant crystal phase, the examples have the desired very low thermal expansion values, measured in the temperature range between room temperature and 700 ° C.
  • the bubble quality of this glass was excellent and was ⁇ 3 bubbles / kg glass.
  • a studded glass band of 4 mm thickness was produced during molding and cooled in a cooling oven to avoid stress. Cooking surfaces of the size 500 x 500 x 4 mm were cut from this glass band and ceramized in a large-scale roller kiln.
  • the ceramization program corresponded to program 2 (Table 2) and the crystallizable glass plates were on a ceramic flat base plate.
  • the glass ceramics obtained had a very good flatness of ⁇ 0.1% in their diagonal dimensions.
  • the transmission curve of this glass-ceramic according to the invention is in Fig. 2 of the comparative glass-ceramic of Example 17 and Example 19 of the present invention.
  • the transmission curve of the glass ceramic according to the invention which is advantageous for the higher display capability is found at values above 0.1% and the good UV blocking below 350 nm.
  • the hob has, for example, a two-dimensional glass ceramic plate 2 with round cooking zones 3, in the present example, four cooking zones. 3
  • the operating field 4 comprises a rotary switch 5 for each cooking plate 3.
  • the rotary switches 5 being designed in a known manner and the cooking surfaces being able to actuate either infinitely or with steps with respect to the heating power.
  • maps 6 are present, which indicate the user via simple symbols to which hotplate 3 the respective switch 5 belongs.
  • a safety and warning field 7 is provided in a side region of the plate 2, preferably in another side region of the plate 2.
  • the security and warning field 7 includes, for example, 2 rows of displays. Present are displays 8, for example for a device fault and displays 9 indicating a temperature condition. Im in FIG. 1 shown example three mutually arranged displays 8 for errors of the entire device and adjacent three mutually arranged displays for the temperature state of the cooking zones 3 are arranged. In this embodiment, the user is thus informed that one of the surfaces is possibly in an elevated temperature state and / or the device or device parts have errors.
  • FIG. 2 are also four cooking zones 3 arranged in the glass ceramic plate 2, wherein the operation panel 4 also has four rotary switch 5 and for each rotary switch 5 a symbol regarding the assignment of the rotary switch 5 is present. Adjacent to each of the rotary switches 5, temperature condition display elements 9 are provided, so that in this embodiment, the temperature state of each hotplate 3 is located adjacent to its rotary switch 5 and the symbology belonging to the plate. In the safety and warning field 7 there are three superimposed error displays 8, which can display an error or normal state for the entire device.
  • FIG. 3 dispenses with a separate safety and warning field 7, wherein the displays 9 are arranged for representing a temperature condition and the error displays 8 each for a cooking position 3 in addition to the respective rotary switch 5.
  • the temperature state of each hotplate 3 and the fault state of each hotplate 3 are individually displayed to the user.
  • three temperature displays 9 and three error displays 8 are arranged in a safety and warning field 7, for example in two columns.
  • a high flame temperature display 9a may have a corresponding flame symbol 10a and a reduced flame mark 10b may be present in a high but not critical temperature display 9b.
  • a critical fault condition indication panel 8a may have a symbol 11a indicative of a critical failure.
  • a display field 8b for indicating an error that does not affect the reliability for example, a corresponding smaller or less clear symbol 11 b may be present.
  • the character arrangement according to FIG. 4 can of course be transferred to the three embodiment, so that the corresponding signals are also arranged next to the rotary switches or other locations of the glass ceramic plate 2.
  • a single display 8 and a single display 9 can be arranged in a safety and warning field 7.
  • any cooking surface i. also each rotary switch 5 each have a display 8, 9 assigned.
  • the temperature display 9 or the fault indicator 8 may also be present in the form of luminaires or segments of different colors arranged along a circle, the colors being green, for example, in an uncritical region (for freedom from misalignment) and blue (for no high temperature), and along the circle rising temperature and / or increasing error rate are displayed with changing colors.
  • these temperature profiles can also be displayed along a bar.
  • the invention has been disclosed with reference to a hob, in particular a hob with a glass ceramic plate. However, the invention is equally applicable to any form of electrical appliances, especially in the home.

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  • Ceramic Engineering (AREA)
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  • Dispersion Chemistry (AREA)
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EP2588426B1 (fr) * 2010-06-30 2023-07-12 Eurokera S.N.C. Dispositif de cuisson
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CN102348658A (zh) 2012-02-08
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CN102348658B (zh) 2016-04-13
DE102009013127B9 (de) 2015-04-16
JP2016064981A (ja) 2016-04-28
JP2012520226A (ja) 2012-09-06
DE102009013127B4 (de) 2014-12-31
WO2010102859A1 (de) 2010-09-16
DE102009013127A1 (de) 2010-09-16
US20120067865A1 (en) 2012-03-22
JP5988587B2 (ja) 2016-09-07
US9156727B2 (en) 2015-10-13
PL2406195T3 (pl) 2021-07-12
EP2406195A1 (de) 2012-01-18

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